CN105980589A - High-carbon steel wire having superior wire drawing properties and method for producing same - Google Patents
High-carbon steel wire having superior wire drawing properties and method for producing same Download PDFInfo
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- CN105980589A CN105980589A CN201580008557.2A CN201580008557A CN105980589A CN 105980589 A CN105980589 A CN 105980589A CN 201580008557 A CN201580008557 A CN 201580008557A CN 105980589 A CN105980589 A CN 105980589A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
- C21D9/54—Furnaces for treating strips or wire
- C21D9/64—Patenting furnaces
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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Abstract
The present invention provides: a wire having consistently favorable wire drawing properties during actual production; and a method for producing the wire. The wire is characterized in that: the composition thereof includes, in terms of mass%, 0.7-1.2% C, 0.1-1.5% Si, at most 1.0% Mn and at most 0.005 ppm N, with the remainder comprising Fe and unavoidable impurities; at least 80% of the cross section of the wire has a bainite structure, with the remaining structures being non-bainite structures; the half-peak width in the (211) crystal plane of a ferrite phase in the structures of the wire cross section is at most 0.6 degrees; the tensile strength (TS) (MPa) and draw (RA) (%) satisfy formula (1) and formula (2); and the standard deviation of the hardness distribution in the cross section being less than 6 in terms of the Vickers hardness (Hv). Formula (1) TS <= 580 + 700 x [C] Formula (2) RA >= 100 - 46 x [C] - 18 x [Mn] - 10 x [Cr]...(2).
Description
Technical field
The present invention relates to need carbon steel wire rod with high or the face of a wire drawing before final toughening or oil-temper
To ACSR (Aluminum Conductor Steel Reinforced: steel-cored aluminium strand) and rope
(rope) carbon steel wire rod with high and manufacture method thereof.
Background technology
Mainly effectively utilizing drawing processing in the secondary operations of wire rod, general employing passes through steyr
(Stelmor) method of rubbing or lead bath toughening have carried out the pearlitic steel of heat treatment.Particularly, STC (Steel
Cord: steel cord) ultrafine wire and the rope in thin footpath use following operation to manufacture: for thin footpath
Change to the line footpath of regulation and implement middle toughening or thin for roll line footpath footpath is answered to reduce Wire Drawing
Become；Etc..
On the other hand, as the way making Wire Drawing strain itself improve, effectively utilize low intensive
Pearlitic structrure and/or bainite structure are well-known.
These tissues, upper by the early strength of wire rod or the tensile strength that obtained by Wire Drawing
The amplitude of liter suppresses relatively low, adds the pulling capacity in man-hour from reducing drawing and controls the viewpoint of processing caloric value
Set out, it is proposed that the dominance in terms of processing unit consumption or material can be expected and have employed two sections of phases
The manufacture method (for example, referring to patent documentation 1 to 3) of the bainite wire rod become.
But, about bainite line, although disclose the heat treatment controlling class frequency, but the brightest
Really for the tissue factor of stably low-intensity.
Citation
Patent documentation
Patent documentation 1: Japanese Unexamined Patent Publication 06-330240 publication
Patent documentation 2: Japanese Unexamined Patent Publication 06-73502 publication
Patent documentation 3: Japanese Unexamined Patent Publication 06-73501 publication
Summary of the invention
The present invention is conceived to above-mentioned situation and completes, and its objective is that offer has in actual manufacture
The wire rod of stable and good Wire Drawing characteristic and the manufacture method of this wire rod.
Patent documentation 1～3 disclosed invention is all by keeping certain time at 350 DEG C～500 DEG C
Within come from overcooling austenite tissue beginning bainitic transformation, then make temperature increase, and keep
Being fully completed to bainitic transformation, thus generate the bainite group that the cementite of precipitation is thicker
Knit.That is, the feature of patent documentation 1～3 disclosed invention is all by upper bayesian in two sections of heat treatments
Soma's softening, is not pointed towards realizing completing of bainitic transformation by first paragraph heat treatment.
The present inventor, in order to obtain good Wire Drawing characteristic with bainite line, have studied at two sections cold
But the softening mechanism in, it was found that: (i) is by remaining to bainite phase in first paragraph heat treatment
Till having become, bainite divides rate to improve, and the cementite being capable of in bainite structure is equal
Even dispersion；(ii) even if initial stage tissue is the single bainite structure of hard, due in two-step cooling
Heating produced by annealing effect, also can meet the wire strength as target；And, (iii)
The tissue point rate that can not be affected by non-bainite structure and make Wire Drawing hardening ratio decline, thus
Complete the present invention.
The present invention completes based on above-mentioned opinion, and its main idea is as follows.
(1) wire rod of a kind of excellent in wire-drawing workability, it is characterised in that become to be grouped in terms of quality %,
Containing C:0.7～1.2%, Si:0.1～1.5%, below Mn:1.0%, below N:0.005%,
Surplus comprises Fe and inevitable impurity, and in wire rod cross section, more than 80% is bainite structure,
Remaining tissue is non-bainite structure, and, the ferritic phase in the tissue in described wire rod cross section
(211) a width of less than 0.6 ° of the half-peak of crystal face, and, tensile strength TS (MPa) and section are received
Shrinkage RA (%) meets following formula (1) and following formula (2) respectively, and the hardness in cross section is divided
The standard deviation of cloth is less than 6 in terms of Vickers hardness (Hv),
TS≤580+700×[C]···(1)
RA≥100-46×[C]-18×[Mn]-10×[Cr]···(2)
Wherein, [C], [Mn] and [Cr] represents the matter of C, Mn and Cr respectively
Amount %.
(2) according to the wire rod of the excellent in wire-drawing workability described in (1), it is characterised in that described one-tenth
Be grouped in terms of quality %, possibly together with below Cr:1.0%, below Ni:1.0%, Cu:0.1% with
Under, below V:0.1%, below Mo:0.5%, below Ti:0.05%, below Nb:0.1%,
Among below Al:0.1%, below Ca:0.05% and below B:0.005% one or both with
On.
(3) manufacture method of the wire rod of a kind of excellent in wire-drawing workability described in above-mentioned (1) or (2),
It is characterized in that, after the hot rolling of steel billet that the one-tenth described in above-mentioned (1) or (2) is grouped into is become wire rod,
Coil into web-like at 850～1050 DEG C, then, be immersed in fuse salt or the fusion of lead of 300～475 DEG C
In complete bainitic transformation so that bainite point rate is more than 80%, then, 550～650
DEG C fuse salt or fusion of lead in impregnate more than 1 second.
(4) manufacture method of the wire rod of a kind of excellent in wire-drawing workability described in above-mentioned (1) or (2),
It is characterized in that, the wire rod that the one-tenth described in above-mentioned (1) or (2) is grouped into is heated to 850 DEG C
Above, then, it is immersed in sand, fuse salt or the fusion of lead of 300～475 DEG C and carries out at toughening
Reason, in wire rod cross section formed more than 80% bainite structure, then, utilize sand, fuse salt,
Fusion of lead, energising or sensing heating are heated more than 1 second at 550～650 DEG C.
In accordance with the invention it is possible to harden with processing can be reduced based on the softening mechanism about bainite
The opinion of the tissue point rate of rate provides the wire rod of Wire Drawing excellent.
Accompanying drawing explanation
Fig. 1 is an example of the relation representing tensile strength TS (MPa) and C amount (quality %)
Figure.
Detailed description of the invention
Hereinafter, the present invention will be described.
The wire rod of the excellent in wire-drawing workability of the present invention is (hereinafter sometimes referred to " wire rod of the present invention ".),
It is characterized in that, become be grouped in terms of quality %, containing C:0.7～1.2%, Si:0.1～1.5%,
Below Mn:1.0%, surplus comprises Fe and inevitable impurity, in wire rod cross section more than 80%
For bainite structure, remaining tissue is non-bainite structure, and, in the tissue in described wire rod cross section
A width of less than 0.6 ° of the half-peak of (211) crystal face of ferritic phase, and, tensile strength TS (MPa)
Following formula (1) and (2) is met, hard in wire rod cross section with contraction percentage of area RA (%)
In the distribution of degree, its standard deviation is less than 6 in terms of Vickers hardness (Hv).
Furthermore, described wire rod cross section refers to the cross section vertical with the length direction of wire rod.
TS≤580+700×[C]···(1)
RA≥100-46×[C]-18×[Mn]-10×[Cr]···(2)
Wherein, [C], [Mn] and [Cr] represents the matter of C, Mn and Cr respectively
Amount %.
First, the restriction reason being grouped into the one-tenth of wire rod of the present invention illustrates.Hereinafter, % means
Quality %.
C:0.7～1.2%
C is to make the cementite point rate of bainite structure and number density and dislocation density increase improve
The element of intensity.When less than 0.7%, it is difficult to ensure that bayesian due to ferrite transformation during heat treatment
Body divides rate, is therefore set as more than 0.7%.It is preferably more than 0.9%.On the other hand, when more than 1.2%
Time, just analysis cementite separates out, and wire-drawing workability deteriorates, and is therefore set as less than 1.2%.It is preferably
Less than 1.0%.
Si:0.1～1.5%
Si is deoxidant element, or the element strengthened by higher content.When less than 0.1%, zinc-plated
Time the generation of alloy-layer unstable, be therefore set as more than 0.1%.It is preferably more than 0.4%.Separately
On the one hand, when more than 1.5%, can promote decarburization during heating, mechanical descaling skin deteriorates, bayesian
Carbide Precipitation during body phase transformation also postpones, and is therefore set as less than 1.5%.It is preferably less than 1.2%.
Below Mn:1.0%
Mn is deoxidant element, or improves the element of hardenability.Suppression heat treatment time ferritic
Generate, but when more than 1.0%, there is phase change delay and generate the probability of non-phase-change organization, therefore
It is set as less than 1.0%.It is preferably less than 0.7%.Lower limit without particular limitation of, but from the group of bainite
Rate of knitting increases this point and sets out, and preferably more than 0.2%, more preferably more than 0.3%.
Wire rod of the present invention, in addition to above-mentioned element, it is also possible in the characteristic not hindering wire rod of the present invention
In the range of Cr, Ni, Cu, V, Mo, Ti, Nb, Al, Ca and B containing suitable amount
In one or more.
Below Cr:1.0%
Cr is the element improving hardenability, ferrite transformation when being to play suppression heat treatment, pearlite
The element of the effect of phase transformation.When more than 1.0%, in addition to the phase transformation end time is elongated, machinery removes
Firecoat deteriorates, and is therefore set as less than 1.0%.It is preferably less than 0.7%.Lower limit includes 0%,
But from reliably obtaining additive effect this point, preferably more than 0.05%.
Below Ni:1.0%
Ni is the element improving hardenability, is suppression ferrite transformation thus improves the class frequency of bainite
Element.When more than 1.0%, the phase transformation end time is elongated, is therefore set as less than 1.0%.Excellent
Elect less than 0.7% as.Lower limit includes 0%, but from reliably obtaining additive effect this point, excellent
Elect more than 0.05% as.
Below Cu:0.1%
Cu is the element improving corrosion resistance.When more than 0.1%, react with S, at Ovshinsky
CuS segregation in body crystal boundary, becomes the bloom in wire rod manufacture process, wire rod etc. and the reason of damage occurs,
Therefore less than 0.1% it is set as.It is preferably less than 0.07%.Lower limit includes 0%, but from reliably obtaining
Set out to additive effect this point, preferably more than 0.01%.
Below V:0.1%
V is the element playing the effect making ferrite transformation postpone under solid solution condition.When more than 0.1%
Time, austenite being formed nitride, makes hardenability decline, during intensification after the phase change, carbide is analysed
Going out, the toughness of line declines, and is therefore set as less than 0.1%.It is preferably less than 0.05%, more preferably
Less than 0.03%.Lower limit includes 0%, but from reliably obtaining additive effect this point, is preferably
More than 0.01%.
Below Mo:0.5%
Mo is to make hardenability improve, suppression ferrite transformation and pearlitic transformation, make the group of bainite
Knit the element that rate improves.When more than 0.5%, in addition to the phase transformation end time is elongated, after the phase change
Intensification time generate carbide, cause post-curing, be therefore set as less than 0.5%.It is preferably 0.3%
Below.Lower limit includes 0%, but from reliably obtaining additive effect this point, preferably 0.1%
Above.
Below Ti:0.05%
Ti be make γ particle diameter fine and by the tissue miniaturization being subsequently formed, contribute to ductility improve
Element.When more than 0.05%, additive effect is saturated, is therefore set as less than 0.05%.Preferably
It is less than 0.02%.Lower limit includes 0%, but from reliably obtaining additive effect this point, excellent
Elect more than 0.005% as.
Below Nb:0.1%
Nb is the element improving hardenability, it addition, be its nitride as pinning particle play a role from
And the element of the control of transformation time when contributing to heat treatment and particle diameter.When more than 0.1%, phase transformation
End time is elongated, is therefore set as less than 0.1%.It is preferably less than 0.07%.Lower limit includes 0%,
But from reliably obtaining additive effect this point, preferably more than 0.005%.
Below Al:0.1%
Al is as the effective element of deoxidant element.When more than 0.1%, generate hard inclusions thing,
Wire-drawing workability declines, and is therefore set as less than 0.1%.It is preferably less than 0.07%.Lower limit includes
0%, but from reliably obtaining additive effect this point, preferably more than 0.02%.
Below Ca:0.05%
Ca is deoxidant element, or the effective element of control to the form of steel inclusion.When exceeding
When 0.05%, thick field trash can be generated, therefore the upper limit is set as less than 0.05%.It is preferably 0.02%
Below.Lower limit includes 0%, but from reliably obtaining additive effect this point, preferably 0.001%
Above.
Below B:0.005%
B be under solid solution B state in crystal boundary generation segregation thus the element suppressing ferrite to generate.When
During more than 0.005%, separate out M at crystal boundary23(C, B)6, stringiness declines, is therefore set as 0.005%
Below.It is preferably less than 0.002%.Lower limit includes 0%, but from reliably obtain additive effect this
Point sets out, and preferably more than 0.0003%.
Below N:0.005%
Nitrogen (N) nitride forming element such with Al, Ti is combined and forms precipitate in steel,
Pinning particle as austenite grain boundary plays a role.It addition, the N meeting existed as solid solution element
Section shrinkage value during tension test is made to decline.Furthermore, when N amount is more than 0.005%, austenite
Crystal boundary becomes trickle, it is difficult to obtain the bainite structure as target, and the section shrinkage value of wire rod
Decline, therefore its higher limit is set as 0.005%.
Then, the tissue of wire rod of the present invention is illustrated.
The tissue of wire rod of the present invention, is characterized in that, in wire rod cross section, in terms of area occupation ratio, 80% with
Upper is bainite structure, and remainder is non-bainite structure, and, the tissue in described wire rod cross section
In a width of less than 0.6 ° of the half-peak of (211) crystal face of ferritic phase.
In order to improve the class frequency of bainite, need the austenitic state from heating to suppress ferrite as far as possible
Phase transformation and pearlitic transformation (being diffusion phase transformation) and be cooled to the temperature of regulation.But, online footpath
Slightly, in the case of the alloying component that hardenability is low, it is difficult to improve tissue, be difficult to make in actual manufacture
The class frequency of non-bainite structure becomes 0%.
Therefore, the present inventor attentively have studied non-bainite structure will not be to overall wire rod and wire drawing
The scope that the intensity of the line after processing impacts.Itself found that: if non-bainite structure is less than
20%, then the intensity of the line after overall wire rod and Wire Drawing will not be impacted.Based on this
Opinion, in wire rod cross section, bainite structure is defined as more than 80%.
Point rate of bainite structure, it is possible to obtain by the following method, it may be assumed that by the length side with wire rod
Produce sample to vertical cross section as sightingpiston, sightingpiston is ground, nitric acid ethanol corrosion
Corrosion, carries out Lepera reagent corrosion as required, use optical microscope or ultramicroscope,
Or X-ray diffraction method is observed.By optical microscope or ultramicroscope being utilized to obtain
Microstructure picture two-value turn to white and black carry out image analysis, it is possible to obtain the area of bainite
Rate.Furthermore, it is also possible to for the sample produced from the optional position of steel plate, by the 1/4 of thickness of slab direction
Portion is set to more than at 3, in employing in the scope of 1000 times of lower shooting 300 × 300 μm, shooting visual field
The method stated measures tissue point rate.Bainite structure and non-bainite structure, it is also possible to by using
KAM method (Kernel Average Misorientation) is to by EBSD (Electron Backscatter
Diffraction: EBSD) obtained by the crystal orientation determination data of electronogram enter
Row parsing differentiates.
Bainite structure is made up of carbide and the ferritic phase of nodular cementite.The shellfish of wire rod of the present invention
Point rate of family name soma, essentially by comprising the heating after coiling process described later and the shellfish of cooling
Family name's body phase transformation operation determines.
And then, present inventor have discovered that and heated by the wire rod carried out after bainitic transformation is completed
Heat treatment step described later, the half-peak of (211) crystal face of the ferritic phase in the tissue in wire rod cross section
Wide decline, the wire rod that can obtain having good wire-drawing workability when a width of less than 0.6 ° of half-peak is strong
Degree.
Furthermore, half-peak breadth means in the diffraction maximum of certain crystal face being measured to by X-ray diffraction,
The width of the angle of the position of the half of peak heights.Owing to pearlitic structrure comprises the elastic strain of many,
Therefore the half-peak breadth in generation phase uprises, even and if heat, it is also difficult to as bainite that
Sample half-peak breadth declines.Thus, owing to pearlite divides rate the highest, half-peak breadth is the highest, is therefore suitable as
The evaluation index of the tissue for generating.
(211) crystal face of ferritic phase in the tissue in wire rod cross section, also with the tissue in this wire rod cross section
In the dispersity of carbide of nodular cementite and the containing ratio of pearlite associate nearly.Cause
This, half-peak breadth becomes the carbon of the nodular cementite judged in the bainite point rate of wire rod, bainite structure
The parameter of the size of the dispersity of compound and the containing ratio of pearlite.It practice, half-peak breadth has
The tendency reduced along with the increase of bainite point rate.It addition, half-peak breadth has dividing along with cementite
Bulk state become uniformly and reduce, along with the pearlite as non-bainite structure containing ratio increase and
The tendency increasing, reducing along with the decline of intensity of wire rod.
Then, the mechanical property of wire rod of the present invention is illustrated.
Wire rod of the present invention, is characterized in that, tensile strength TS (MPa) and contraction percentage of area RA (%)
Meet following formula (1) and following formula (2) respectively.
TS≤580+700×[C]···(1)
RA≥100-46×[C]-18×[Mn]-10×[Cr]···(2)
Here, [C], [Mn] and [Cr] represents the matter of C, Mn and Cr respectively
Amount %.
Tensile strength TS of bainite wire rod and contraction percentage of area RA, depend on cementite particle
Average headway, dislocation density and block particle diameter.Particularly, in wire rod of the present invention, depend on
Cementite divides rate corresponding carbon amounts.The present inventor has investigated at the class frequency of bainite and ferrite
Tensile strength TS and the relation of carbon amounts ([C]) in the prescribed limit of the half-peak breadth of phase, it addition, adjust
Look into the pass of contraction percentage of area RA and " 100-46 × [C]-18 × [Mn]-10 × [Cr] "
System.
" 100-46 × [C]-18 × [Mn]-10 × [Cr] " is the representative hindering section shrinkage
The amount of property element is multiplied by the index affecting coefficient to evaluate comprehensive impact.By specifying this index
Lower limit, it is possible to give the feature in mechanical property to wire rod of the present invention.
Fig. 1 illustrates the result of investigation tensile strength TS and the relation of carbon amounts ([C]).Understand tension
Intensity meets above-mentioned formula (1).About contraction percentage of area RA, the inventors discovered that if on Man Zuing
State formula (2) the best.
Hardness distribution in cross section also has influence on wire drawing characteristic.Find: hard by wire rod cross section
In degree distribution, its standard deviation is set smaller than 6 in terms of Vickers hardness (Hv), just can obtain good
The wire rod of wire drawing characteristic.
Then, the manufacture method of wire rod of the present invention is illustrated.
The manufacture method of wire rod of the present invention, it is characterised in that the steel that the one-tenth of wire rod of the present invention is grouped into
After base hot rolling becomes wire rod, coil into web-like at 850～1050 DEG C, then, be immersed in 300～475
DEG C fuse salt or fusion of lead in complete bainitic transformation so that bainite point rate be 80% with
On, then, impregnate more than 15 seconds in the fuse salts of 550～650 DEG C or fusion of lead.
After the hot rolling of steel billet that the one-tenth of wire rod of the present invention is grouped into is become wire rod, coil into line during web-like
Material temperature is critically important in terms of adjusting austenite particle diameter.The coiling temperature of wire rod is according to the hardenability of steel grade
Change, but when more than 1050 DEG C, it is difficult to physically carry out terminal processes, be therefore set as 1050
Below DEG C.It is preferably less than 1000 DEG C.
On the other hand, when coiling temperature is less than 850 DEG C, austenite particle diameter attenuates, and hardenability declines,
And the coexistence region decarburization of skin section can be carried out, be therefore set as more than 850 DEG C.Be preferably 900 DEG C with
On.
It addition, the manufacture method of wire rod of the present invention, it is characterized in that, the one-tenth of wire rod of the present invention is grouped into
Wire rod be heated to more than 850 DEG C, then, be immersed in sand, the fuse salt or molten of 300～475 DEG C
Melt and lead carries out patent, the bainite structure of formation more than 80% in wire rod cross section, then,
Utilize sand, fuse salt, fusion of lead, energising or sensing heating 550～650 DEG C heating 1 second with
On.
Heating-up temperature in the case of making it carry out bainitic transformation the heating of temporary transient chilled wire rod,
Have influence on the hardenability of steel.When heating-up temperature is less than 850 DEG C, austenite particle diameter attenuates, and hardens
Property decline, a point rate for bainite does not improves, and carries out the coexistence region decarburization of skin section, is therefore set as
More than 850 DEG C.It is preferably more than 900 DEG C.
In order to control austenite grain is carried out the particle of pinning, set according to the amount of alloying element and add
Hot temperature, although the upper limit of heating-up temperature determines the most especially, but from the point of view of economy this point, preferably
It it is less than 1150 DEG C.More preferably less than 1100 DEG C.
To the wire rod after hot rolling of steel billet or by the line after temporary transient chilled described wire rod reheating
Material carries out the temperature (that is, coolant temperature) of the sand, fuse salt or the fusion of lead that impregnate, shadow
Ring the bainitic transformation temperature to described wire rod and rate of cooling.When coolant temperature is more than 475
DEG C time, rate of cooling declines, and pearlitic transformation occurs, it is difficult to realize the shellfish in the whole cross section of wire rod
Family name's body, is therefore set as less than 475 DEG C.It is preferably less than 450 DEG C.
On the other hand, when coolant temperature is less than 300 DEG C, bainitic transformation is changed for a long time, because of
This is set as more than 300 DEG C.It is preferably more than 350 DEG C.
After the present invention can be by being heated to more than 850 DEG C by temporary transient chilled described wire rod, by institute
State wire rod 300～475 DEG C temperature range keep, make the bainitic transformation of described wire rod tissue enter
OK, the bainite structure making described wire rod is uniform.This is because, under this carbon amounts, bainite structure
Main generation at a temperature of about 300 DEG C～about 500 DEG C, but the size of bainite structure is by this bayesian
The impact of the temperature during generation of soma.
By described wire rod being maintained at the temperature range of 300～475 DEG C until bainitic transformation completes
Till, it is possible to the bainite structure making described wire rod is uniform.But, from the viewpoint of manufacturing cost
Keep the most for a long time.
On the other hand, before completing at bainitic transformation, wire rod is heated to above 475 DEG C and keeps rule
When fixing time above, although bainitic transformation completes, but bainite structure becomes uneven, wire rod
The hardness distribution in cross section becomes uneven, the most preferred.
Therefore, in the present invention, described wire rod is kept the temperature range of 300～475 DEG C, until
Till among tissue in wire rod cross section, bainite structure reaches more than 80%, then, as be described hereinafter that
Sample heats more than 1 second at 550～650 DEG C.
Furthermore, until retention time of completing of bainitic transformation or until bainite point rate reaches
Retention time to more than 80% can determine previously according to the experiment condition of regulation.Such as,
Can investigate in advance at the composition with wire rod, impregnation process in fuse salt or fusion of lead or toughening
Temperature and bainite when retention time, described impregnation process or the patent managed divide the right of rate
Should be related to, determine the described retention time based on survey result.In this case, bainitic transformation
Degree needs are the most corresponding with measured value to be judged.Even it addition, the manufacturer of test being not carried out
Method, it is also possible to based on the bainite structure under close known manufacturing condition and this manufacturing condition
The relation of point rate carry out interpolation or extrapolation, it was predicted that use described unenforced manufacture method manufacture
Point rate of bainite structure of wire rod, and determine the described retention time.Or, it is also possible to want
Making sample under the identical manufacturing condition of manufacturing condition implemented, one side confirms the manufacturing process way of wire rod
In point rate of bainite structure, one side carries out the manufacture of wire rod.
Carry out the heat treatment step of the heating of the wire rod after being completed by bainitic transformation.In this heat treatment step
Heating-up temperature have influence on reply and the softening of bainite line.When heating-up temperature is less than 550 DEG C,
Can not obtain sufficient softening effect, therefore heating-up temperature is set as more than 550 DEG C.It is preferably 570
More than DEG C.When more than 650 DEG C, cementite carries out Ostwald's growth, the ductility of wire rod
Decline, be therefore set as less than 650 DEG C.It is preferably less than 630 DEG C.
Bainitic transformation complete after heat time heating time, adjust according to heating-up temperature, but soft in order to make
Change is carried out, and is set as more than 1 second.Between when heated long time, cementite carries out Ostwald
Growth, ductility declines, but as long as suitably adjusting in the range of heating-up temperature, the therefore upper limit
Set the most especially.It addition, until reach the time of above-mentioned heating-up temperature or until reach above-mentioned
Programming rate till heating-up temperature without particular limitation of.
Furthermore, about heating, except being immersed in the sand of set point of temperature, fuse salt or fusion of lead
Beyond carrying out, it would however also be possible to employ energising or sensing heating are carried out.
Then, embodiments of the invention are illustrated.Condition in embodiment is to confirm this
Bright exploitativeness and effect and a condition example using, the present invention is not by this condition example
Limit.Without departing from idea of the invention, the purpose of the present invention can be reached limit under the present invention can adopt
Use various condition.
Embodiment
By the one-tenth shown in table 1 being grouped into the wire rod of A～O at " cooling condition " shown in table 2-1
Shown in set point of temperature under keep the stipulated time make it complete bainitic transformation.Implement following heat
Process, i.e. the wire rod after being completed by bainitic transformation is heated separately to " after bainitic transformation completes
Heat treatment condition " shown in set point of temperature, under this set point of temperature keep the stipulated time.At table 2-2
Shown in tensile strength TS (MPa) of wire rod after heat treatment and the mensuration of the contraction percentage of area (%)
The measurement result of the half-peak breadth of the ferritic phase in result and bainite structure rate and this bainite structure,
And the distribution of the hardness in wire rod cross section.Furthermore, about the transformation time of bainite, after by hot rolling
Wire rod directly carry out heat treatment in the case of, made it suitably change 300 seconds as the upper limit,
In the case of wire rod after reheating carries out patent, made it suitable using 1800 seconds as the upper limit
Change.
Furthermore, respective at example 1,2,6～8,10,12,13 and comparative example 1～6
In manufacture, employ the hot rolling of steel billet being grouped into by the one-tenth shown in table 1 under conditions of shown in table 2-1
And the wire rod obtained.It addition, example 3～5,9,11 and each wire rod of comparative example 7, it is to adopt
With the manufacture method manufacture comprising following operation: producing the wire rod that the one-tenth shown in table 1 is grouped into
After it is temporarily cooled down, described wire rod is reheated under the heating-up temperature shown in table 2-1.
The composition of the steel grade K of table 1 is corresponding to the composition of the steel wire of patent documentation 3.To have these groups
The wire rod become keeps the stipulated time under the set point of temperature in " cooling condition " shown in table 2-1, by
This is until bainitic transformation completes to make in the past the bainitic transformation of the wire rod of comparative example 6 to carry out.Then,
Implement following heat treatment: the wire rod of comparative example 7 is heated to " bainitic transformation complete after heat treatment
Condition " shown in set point of temperature, under this set point of temperature keep the stipulated time, complete bainite
Phase transformation.
For the mensuration of bainite structure rate, employ electron beam back scattering diffraction method (EBSD).?
Regions more than 300 μ m 180 μm is measured by the central part of wire rod, uses KAM (Kernel
Average Misorientation) method, the region not causing Crystal Rotation is defined as bainite structure,
And calculate bainite point rate.
For the mensuration of the half-peak breadth of ferritic phase, use X-ray diffraction device, the ray of X-ray
Source employs Cr pipe ball.Mensuration face is set to (211) face, carries out maximum count and reaches more than 3000
The mensuration of time, using its half-peak breadth as measured value.
It addition, for example 1～13 and the wire rod of comparative example 1～7 investigated steel grade the most in advance
Composition and the corresponding relation of manufacturing condition and point rate of bainite structure of heat treatment etc..Based on this
The survey result of sample judges the degree of the carrying out of the bainitic transformation of the tissue of wire rod, thus to invention
Example 1～13 and the bainitic transformation of wire rod of comparative example 1～7 whether start and whether complete to carry out
Judge.
For the distribution of the hardness in wire rod cross section, use Vickers pyramid hardness testing machine, to obtained tissue
The cross section of length direction, beat trace with what the load of 1kgf had carried out 100 points.By its standard deviation
Deviation as hardness.
Example 1～13 is embodiments of the invention, as shown in table 2-2, has obtained Wire Drawing special
Property excellent bainite wire rod.
In comparative example 1, the coiling temperature after billet rolling is low, time in time batching to cooling, carries out
Ferrite transformation, it is impossible to obtain the bainite structure point rate of target.It addition, tensile strength TS is the most not
Meet formula (1).
In comparative example 2 and comparative example 3, hardenability improves elements Si and Mn exceedes rule respectively
Fixed scope, hardenability becomes too high, and therefore the phase transformation in cooling first paragraph does not complete.Comparing
In example 4, the temperature in cooling first paragraph has exceeded the scope of regulation, therefore cools down slack-off, produces relatively
Many pearlite, result is the bainite structure point rate not obtaining target.
In comparative example 5, not carrying out cooling down the heating in second segment, therefore half-peak breadth has exceeded rule
Fixed value, tensile strength TS is also unsatisfactory for formula (1).In comparative example 6, C amount has exceeded regulation
Scope, in the cooling started from austenite generate cementite, contraction percentage of area RA is unsatisfactory for formula
(2)。
In comparative example 6, before bainitic transformation completes, wire rod is heated, therefore bainite structure
Become uneven, the hardness skewness in wire rod cross section.Thus, in comparative example 6, section is received
Shrinkage RA is unsatisfactory for formula (2), and the ductility of wire rod declines, its Wire Drawing characteristic step-down.
Industrial applicability
As described above, according to the present invention, softening mechanism based on bainite processes firmly with reducing
The opinion that the class frequency of rate relates to, using the teaching of the invention it is possible to provide the wire rod of Wire Drawing excellent.Therefore, originally
Invention is the technology that utilizability is high in wire rod manufacturing industry.
Claims (4)
1. the wire rod of an excellent in wire-drawing workability, it is characterised in that become to be grouped in terms of quality %,
Containing C:0.7～1.2%, Si:0.1～1.5%, below Mn:1.0%, below N:0.005%,
Surplus comprises Fe and inevitable impurity, and in wire rod cross section, more than 80% is bainite structure,
Remaining tissue is non-bainite structure, and, the ferritic phase in the tissue in described wire rod cross section
(211) a width of less than 0.6 ° of the half-peak of crystal face, and, tensile strength TS and contraction percentage of area RA
Meet following formula (1) and following formula (2) respectively, the standard deviation of hardness in cross section distribution with
Vickers hardness (Hv) meter is less than 6,
TS≤580+700×[C]···(1)
RA≥100-46×[C]-18×[Mn]-10×[Cr]···(2)
Wherein, the unit of described tensile strength TS is MPa, the unit of described contraction percentage of area RA
For %, [C], [Mn] and [Cr] represents quality % of C, Mn and Cr respectively.
The wire rod of excellent in wire-drawing workability the most according to claim 1, it is characterised in that described
Become to be grouped in terms of quality %, possibly together with below Cr:1.0%, below Ni:1.0%, Cu:0.1%
Below, below V:0.1%, below Mo:0.5%, below Ti:0.05%, below Nb:0.1%,
Among below Al:0.1%, below Ca:0.05% and below B:0.005% one or both with
On.
3. a manufacture method for the wire rod of the excellent in wire-drawing workability described in claim 1 or 2, its
It is characterised by,
After the hot rolling of steel billet that one-tenth described in claim 1 or 2 is grouped into is become wire rod, 850～
1050 DEG C coil into web-like, then, are immersed in the fuse salt of 300～475 DEG C or fusion of lead and complete
Bainitic transformation is so that bainite point rate is more than 80%, then, at the fuse salt of 550～650 DEG C
Or fusion of lead impregnates more than 1 second.
4. a manufacture method for the wire rod of the excellent in wire-drawing workability described in claim 1 or 2, its
It is characterised by,
The wire rod that one-tenth described in claim 1 or 2 is grouped into is heated to more than 850 DEG C, then,
It is immersed in sand, fuse salt or the fusion of lead of 300～475 DEG C and carries out patent, cut at wire rod
Form the bainite structure of more than 80% in face, then, utilize sand, fuse salt, fusion of lead, lead to
Electricity or sensing heating are heated more than 1 second at 550～650 DEG C.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2014-044216 | 2014-03-06 | ||
| JP2014044216 | 2014-03-06 | ||
| PCT/JP2015/056691 WO2015133614A1 (en) | 2014-03-06 | 2015-03-06 | High-carbon steel wire having superior wire drawing properties and method for producing same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105980589A true CN105980589A (en) | 2016-09-28 |
| CN105980589B CN105980589B (en) | 2018-01-16 |
Family
ID=54055414
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201580008557.2A Expired - Fee Related CN105980589B (en) | 2014-03-06 | 2015-03-06 | The carbon steel wire rod with high and its manufacture method of excellent in wire-drawing workability |
Country Status (5)
| Country | Link |
|---|---|
| EP (1) | EP3115478B1 (en) |
| JP (1) | JP5900710B2 (en) |
| KR (1) | KR101944599B1 (en) |
| CN (1) | CN105980589B (en) |
| WO (1) | WO2015133614A1 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108823490A (en) * | 2018-06-01 | 2018-11-16 | 张家港保税区恒隆钢管有限公司 | A kind of Automotive Stabilizer Bar seamless steel pipe |
| WO2020113606A1 (en) * | 2018-12-03 | 2020-06-11 | 江苏兴达钢帘线股份有限公司 | Steel cord and manufacturing method therefor, and tire provided with steel cord |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109312436B (en) * | 2016-07-05 | 2021-08-10 | 日本制铁株式会社 | Wire rod, steel wire and member |
| JP6596470B2 (en) * | 2017-07-20 | 2019-10-23 | トクセン工業株式会社 | Medical treatment device wire and guide wire |
| KR102362665B1 (en) * | 2019-12-20 | 2022-02-11 | 주식회사 포스코 | Wire rod, high strength steel wire and method for manufacturing thereof |
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| US5647918A (en) * | 1993-04-06 | 1997-07-15 | Nippon Steel Corporation | Bainite wire rod and wire for drawing and methods of producing the same |
| US5658399A (en) * | 1993-04-06 | 1997-08-19 | Nippon Steel Corporation | Bainite wire rod and wire for drawing and methods of producing the same |
| JP2001220650A (en) * | 1999-11-30 | 2001-08-14 | Sumitomo Electric Ind Ltd | Steel wire, spring and producing method therefor |
| CN101208445A (en) * | 2005-06-29 | 2008-06-25 | 新日本制铁株式会社 | High-strength wire rod having superior rod drawability, manufacturing method therefor |
| CN103080353A (en) * | 2010-08-17 | 2013-05-01 | 新日铁住金株式会社 | Special steel steel-wire and special steel wire material |
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| JP2652099B2 (en) * | 1991-10-24 | 1997-09-10 | 新日本製鐵株式会社 | Method of manufacturing high strength bead wire |
| JP2984888B2 (en) | 1992-06-23 | 1999-11-29 | 新日本製鐵株式会社 | High carbon steel wire or steel wire excellent in wire drawability and method for producing the same |
| JP2984889B2 (en) | 1992-07-08 | 1999-11-29 | 新日本製鐵株式会社 | High carbon steel wire or steel wire excellent in wire drawability and method for producing the same |
| JPH06306481A (en) * | 1993-04-22 | 1994-11-01 | Nippon Steel Corp | Method for heat-treating steel wire using fluidized bed |
| JP3018268B2 (en) | 1993-05-25 | 2000-03-13 | 新日本製鐵株式会社 | High carbon steel wire or steel wire excellent in wire drawability and method for producing the same |
| JP3398207B2 (en) * | 1994-03-18 | 2003-04-21 | 新日本製鐵株式会社 | Manufacturing method of hard drawn steel wire for cold drawing with excellent wire drawing workability and fatigue properties |
| JPH07268487A (en) * | 1994-04-01 | 1995-10-17 | Nippon Steel Corp | Production of high carbon steel wire rod or steel wire excellent in wiredrawability |
| JP3388418B2 (en) * | 1994-06-21 | 2003-03-24 | 新日本製鐵株式会社 | Method for producing high carbon steel wire or steel wire excellent in wire drawing workability |
| JP2002241899A (en) * | 2001-02-09 | 2002-08-28 | Kobe Steel Ltd | High strength steel wire having excellent delayed fracture resistance and excellent forging property and manufacturing method therefor |
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2015
- 2015-03-06 KR KR1020167023858A patent/KR101944599B1/en active IP Right Grant
- 2015-03-06 CN CN201580008557.2A patent/CN105980589B/en not_active Expired - Fee Related
- 2015-03-06 JP JP2015537034A patent/JP5900710B2/en not_active Expired - Fee Related
- 2015-03-06 WO PCT/JP2015/056691 patent/WO2015133614A1/en active Application Filing
- 2015-03-06 EP EP15759266.8A patent/EP3115478B1/en active Active
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5647918A (en) * | 1993-04-06 | 1997-07-15 | Nippon Steel Corporation | Bainite wire rod and wire for drawing and methods of producing the same |
| US5658399A (en) * | 1993-04-06 | 1997-08-19 | Nippon Steel Corporation | Bainite wire rod and wire for drawing and methods of producing the same |
| JP2001220650A (en) * | 1999-11-30 | 2001-08-14 | Sumitomo Electric Ind Ltd | Steel wire, spring and producing method therefor |
| CN101208445A (en) * | 2005-06-29 | 2008-06-25 | 新日本制铁株式会社 | High-strength wire rod having superior rod drawability, manufacturing method therefor |
| CN103080353A (en) * | 2010-08-17 | 2013-05-01 | 新日铁住金株式会社 | Special steel steel-wire and special steel wire material |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN108823490A (en) * | 2018-06-01 | 2018-11-16 | 张家港保税区恒隆钢管有限公司 | A kind of Automotive Stabilizer Bar seamless steel pipe |
| WO2020113606A1 (en) * | 2018-12-03 | 2020-06-11 | 江苏兴达钢帘线股份有限公司 | Steel cord and manufacturing method therefor, and tire provided with steel cord |
Also Published As
| Publication number | Publication date |
|---|---|
| EP3115478A4 (en) | 2017-09-06 |
| CN105980589B (en) | 2018-01-16 |
| EP3115478B1 (en) | 2019-05-01 |
| JPWO2015133614A1 (en) | 2017-04-06 |
| KR101944599B1 (en) | 2019-01-31 |
| EP3115478A1 (en) | 2017-01-11 |
| KR20160114697A (en) | 2016-10-05 |
| WO2015133614A1 (en) | 2015-09-11 |
| JP5900710B2 (en) | 2016-04-06 |
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